EP1441991B1 - A process of making rare earth doped optical fibre - Google Patents

A process of making rare earth doped optical fibre Download PDF

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Publication number
EP1441991B1
EP1441991B1 EP01978809A EP01978809A EP1441991B1 EP 1441991 B1 EP1441991 B1 EP 1441991B1 EP 01978809 A EP01978809 A EP 01978809A EP 01978809 A EP01978809 A EP 01978809A EP 1441991 B1 EP1441991 B1 EP 1441991B1
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Prior art keywords
tube
silica
core
coated
dispersion
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German (de)
English (en)
French (fr)
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EP1441991A1 (en
Inventor
Ranjan Central Glass and Ceramic Research SEN
Miss Minati Central Glass and Ceramic CHATTERJEE
Milan Kanti Central Glass and Ceramic NASKAR
Mrinmay Central Glass and Ceramic Research PAL
Mukul Chandra Central Glass and Ceramic PAUL
Shyamal Kumar Central Glass and Ceramic BHADRA
Kamal Central Glass and Ceramic Research DASGUPTA
Dibyendu Central Glass and Ceramic GANGULI
Tarun Central Glass and Ceramic BANDYOPADHYAY
Aharon Bar-Ilan University GEDANKEN
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Bar Ilan University
Council of Scientific and Industrial Research CSIR
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Bar Ilan University
Council of Scientific and Industrial Research CSIR
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    • C—CHEMISTRY; METALLURGY
    • C03—GLASS; MINERAL OR SLAG WOOL
    • C03B—MANUFACTURE, SHAPING, OR SUPPLEMENTARY PROCESSES
    • C03B37/00—Manufacture or treatment of flakes, fibres, or filaments from softened glass, minerals, or slags
    • C03B37/01—Manufacture of glass fibres or filaments
    • C03B37/012—Manufacture of preforms for drawing fibres or filaments
    • C03B37/014—Manufacture of preforms for drawing fibres or filaments made entirely or partially by chemical means, e.g. vapour phase deposition of bulk porous glass either by outside vapour deposition [OVD], or by outside vapour phase oxidation [OVPO] or by vapour axial deposition [VAD]
    • C03B37/018—Manufacture of preforms for drawing fibres or filaments made entirely or partially by chemical means, e.g. vapour phase deposition of bulk porous glass either by outside vapour deposition [OVD], or by outside vapour phase oxidation [OVPO] or by vapour axial deposition [VAD] by glass deposition on a glass substrate, e.g. by inside-, modified-, plasma-, or plasma modified- chemical vapour deposition [ICVD, MCVD, PCVD, PMCVD], i.e. by thin layer coating on the inside or outside of a glass tube or on a glass rod
    • C—CHEMISTRY; METALLURGY
    • C03—GLASS; MINERAL OR SLAG WOOL
    • C03B—MANUFACTURE, SHAPING, OR SUPPLEMENTARY PROCESSES
    • C03B37/00—Manufacture or treatment of flakes, fibres, or filaments from softened glass, minerals, or slags
    • C03B37/01—Manufacture of glass fibres or filaments
    • C03B37/012—Manufacture of preforms for drawing fibres or filaments
    • C03B37/014—Manufacture of preforms for drawing fibres or filaments made entirely or partially by chemical means, e.g. vapour phase deposition of bulk porous glass either by outside vapour deposition [OVD], or by outside vapour phase oxidation [OVPO] or by vapour axial deposition [VAD]
    • C03B37/018—Manufacture of preforms for drawing fibres or filaments made entirely or partially by chemical means, e.g. vapour phase deposition of bulk porous glass either by outside vapour deposition [OVD], or by outside vapour phase oxidation [OVPO] or by vapour axial deposition [VAD] by glass deposition on a glass substrate, e.g. by inside-, modified-, plasma-, or plasma modified- chemical vapour deposition [ICVD, MCVD, PCVD, PMCVD], i.e. by thin layer coating on the inside or outside of a glass tube or on a glass rod
    • C03B37/01807—Reactant delivery systems, e.g. reactant deposition burners
    • C03B37/01838—Reactant delivery systems, e.g. reactant deposition burners for delivering and depositing additional reactants as liquids or solutions, e.g. for solution doping of the deposited glass
    • C—CHEMISTRY; METALLURGY
    • C03—GLASS; MINERAL OR SLAG WOOL
    • C03B—MANUFACTURE, SHAPING, OR SUPPLEMENTARY PROCESSES
    • C03B37/00—Manufacture or treatment of flakes, fibres, or filaments from softened glass, minerals, or slags
    • C03B37/01—Manufacture of glass fibres or filaments
    • C03B37/012—Manufacture of preforms for drawing fibres or filaments
    • C03B37/014—Manufacture of preforms for drawing fibres or filaments made entirely or partially by chemical means, e.g. vapour phase deposition of bulk porous glass either by outside vapour deposition [OVD], or by outside vapour phase oxidation [OVPO] or by vapour axial deposition [VAD]
    • C03B37/016—Manufacture of preforms for drawing fibres or filaments made entirely or partially by chemical means, e.g. vapour phase deposition of bulk porous glass either by outside vapour deposition [OVD], or by outside vapour phase oxidation [OVPO] or by vapour axial deposition [VAD] by a liquid phase reaction process, e.g. through a gel phase
    • C—CHEMISTRY; METALLURGY
    • C03—GLASS; MINERAL OR SLAG WOOL
    • C03C—CHEMICAL COMPOSITION OF GLASSES, GLAZES OR VITREOUS ENAMELS; SURFACE TREATMENT OF GLASS; SURFACE TREATMENT OF FIBRES OR FILAMENTS MADE FROM GLASS, MINERALS OR SLAGS; JOINING GLASS TO GLASS OR OTHER MATERIALS
    • C03C1/00—Ingredients generally applicable to manufacture of glasses, glazes, or vitreous enamels
    • C03C1/02—Pretreated ingredients
    • C—CHEMISTRY; METALLURGY
    • C03—GLASS; MINERAL OR SLAG WOOL
    • C03C—CHEMICAL COMPOSITION OF GLASSES, GLAZES OR VITREOUS ENAMELS; SURFACE TREATMENT OF GLASS; SURFACE TREATMENT OF FIBRES OR FILAMENTS MADE FROM GLASS, MINERALS OR SLAGS; JOINING GLASS TO GLASS OR OTHER MATERIALS
    • C03C1/00—Ingredients generally applicable to manufacture of glasses, glazes, or vitreous enamels
    • C03C1/02—Pretreated ingredients
    • C03C1/026—Pelletisation or prereacting of powdered raw materials
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B82—NANOTECHNOLOGY
    • B82Y—SPECIFIC USES OR APPLICATIONS OF NANOSTRUCTURES; MEASUREMENT OR ANALYSIS OF NANOSTRUCTURES; MANUFACTURE OR TREATMENT OF NANOSTRUCTURES
    • B82Y30/00—Nanotechnology for materials or surface science, e.g. nanocomposites
    • C—CHEMISTRY; METALLURGY
    • C03—GLASS; MINERAL OR SLAG WOOL
    • C03B—MANUFACTURE, SHAPING, OR SUPPLEMENTARY PROCESSES
    • C03B2201/00—Type of glass produced
    • C03B2201/02—Pure silica glass, e.g. pure fused quartz
    • C—CHEMISTRY; METALLURGY
    • C03—GLASS; MINERAL OR SLAG WOOL
    • C03B—MANUFACTURE, SHAPING, OR SUPPLEMENTARY PROCESSES
    • C03B2201/00—Type of glass produced
    • C03B2201/06—Doped silica-based glasses
    • C03B2201/08—Doped silica-based glasses doped with boron or fluorine or other refractive index decreasing dopant
    • C03B2201/12—Doped silica-based glasses doped with boron or fluorine or other refractive index decreasing dopant doped with fluorine
    • C—CHEMISTRY; METALLURGY
    • C03—GLASS; MINERAL OR SLAG WOOL
    • C03B—MANUFACTURE, SHAPING, OR SUPPLEMENTARY PROCESSES
    • C03B2201/00—Type of glass produced
    • C03B2201/06—Doped silica-based glasses
    • C03B2201/20—Doped silica-based glasses doped with non-metals other than boron or fluorine
    • C03B2201/28—Doped silica-based glasses doped with non-metals other than boron or fluorine doped with phosphorus
    • C—CHEMISTRY; METALLURGY
    • C03—GLASS; MINERAL OR SLAG WOOL
    • C03B—MANUFACTURE, SHAPING, OR SUPPLEMENTARY PROCESSES
    • C03B2201/00—Type of glass produced
    • C03B2201/06—Doped silica-based glasses
    • C03B2201/30—Doped silica-based glasses doped with metals, e.g. Ga, Sn, Sb, Pb or Bi
    • C03B2201/31—Doped silica-based glasses doped with metals, e.g. Ga, Sn, Sb, Pb or Bi doped with germanium
    • C—CHEMISTRY; METALLURGY
    • C03—GLASS; MINERAL OR SLAG WOOL
    • C03B—MANUFACTURE, SHAPING, OR SUPPLEMENTARY PROCESSES
    • C03B2201/00—Type of glass produced
    • C03B2201/06—Doped silica-based glasses
    • C03B2201/30—Doped silica-based glasses doped with metals, e.g. Ga, Sn, Sb, Pb or Bi
    • C03B2201/34—Doped silica-based glasses doped with metals, e.g. Ga, Sn, Sb, Pb or Bi doped with rare earth metals, i.e. with Sc, Y or lanthanides, e.g. for laser-amplifiers
    • C03B2201/36—Doped silica-based glasses doped with metals, e.g. Ga, Sn, Sb, Pb or Bi doped with rare earth metals, i.e. with Sc, Y or lanthanides, e.g. for laser-amplifiers doped with rare earth metals and aluminium, e.g. Er-Al co-doped
    • Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
    • Y02—TECHNOLOGIES OR APPLICATIONS FOR MITIGATION OR ADAPTATION AGAINST CLIMATE CHANGE
    • Y02P—CLIMATE CHANGE MITIGATION TECHNOLOGIES IN THE PRODUCTION OR PROCESSING OF GOODS
    • Y02P40/00—Technologies relating to the processing of minerals
    • Y02P40/50—Glass production, e.g. reusing waste heat during processing or shaping
    • Y02P40/57—Improving the yield, e-g- reduction of reject rates

Definitions

  • the present invention relates to a Process of Making Rare Earth Doped Optical Fibre.
  • High silica based optical fibres are firmly established as the most efficient interconnection media for optical telecommunication networks.
  • the fibres are used as the passive transmission media to guide optical signals over long distances.
  • rare-earth (RE) ions if doped into the core of such fibres, make them optically active due to the characteristic emission of the RE when pumped at suitable wavelengths. Because of this property RE doped fibres have shown great potential for use as active devices for photonic applications like optical amplifiers and fibre lasers at various wavelengths.
  • the fibres are also found to be promising candidates for their application as sensors for monitoring temperature, radiation dose etc.
  • Erbium doped fiber which is the active medium of an EDFA (erbium doped fiber amplifier) has been an enabling technology for optical networks operating in the third telecommunication window between 1530 and 1610 nm.
  • EDFA can simultaneously amplify several optical channels in a single fibre which has enabled the implementation of DWDM (dense wavelength division multiplexing) technology with the potential of increasing the bandwidth of long distance transmission systems from Gb/s to Tb/s ranges.
  • EDFAs exhibit high gain, large bandwidth, low noise, polarisation insensitive gain, substantially reduced cross talk problems and low insertion losses at the operating wavelengths.
  • the deployment of EDFA has spurred a tremendous growth in advanced telecommunication systems replacing the conventional optoelectronic repeaters.
  • EDF Erbium Doped Fibre
  • the prepared tubes are soaked in an alcoholic solution of 1M Al(NO 3 ) 3 + various concentrations of ErCl 3 and NdCl 3 for 1 hour.
  • the tubes are subsequently blown dry and collapsed to make preforms in the usual way.
  • Aluminium (Al) is said to be a key component in producing high RE concentrations in the core centre without clustering effect. It is further disclosed that Al and RE profile lock together in some way which retards the volatility of RE ion. The dip at the core centre is observed both for P and GeO 2 .
  • the desiccation is carried out for a period of 24 -240 hours at a temperature of 60° - 70 °C in an atmosphere of nitrogen gas or inert gas.
  • This desiccated soot preform is heated and dehydrated for a period of 2.5 - 3.5 hours at a temperature of 950° - 1050 °C in an atmosphere of helium gas containing 0.25 to 0.35% chlorine gas and further heated for a period of 3-5 hours at a temperature of 1400° - 1600°C to render it transparent, thereby forming an erbium doped glass preform.
  • the segregation of AlCl 3 in the preform formation process is suppressed due to the presence of phosphorus and as a result, the doping concentration of Al ions can be set to a high level (>3 wt%).
  • the dopant concentration and component ratio of Er, Al and P ions are claimed to be extremely accurate and homogeneous in radial as well as in longitudinal directions.
  • a wide variety of dopant materials, in the form of salts or alkoxides are easily incorporated by dissolving them in the solvent.
  • the method suffers disadvantage that there is a possibility of evaporation of the RE-salts during sintering at high temperature, there by causing inhomogeneous distribution of RE-ions through out the length of the preform.
  • the TEOS dissolved in an alcoholic or aqueous solvent contains required quantity of the dopants, polymerizing the sol to form a gel followed by drying and sintering the tube.
  • the main disadvantage of the method is that there is every possibility of evaporation of the RE salts during sintering at high temperature, resulting in an inhomogeneous distribution of RE-ions throughout the length of the preform.
  • WO-A-01/53223 relates to a sol-gel method of preparing powder for use in forming glass fibres, by forming a mixture of glass precursors and dopants in a solvent, hydrolysing the mixture, inducing or allowing the mixture to condense to form colloidal particles, treating the mixture bromine to remove water and hydroxide groups, drying to form a powder, and calcining to form a calcined powder suitable for processing into a glass.
  • the powder can be formed into glass fibres by depositing a solvent suspension of the powder on the inner surface of a glass tube and heating the tube to convert the suspension into a glass and collapse the tube into a glass fibre.
  • the main object of the present invention is to provide a process for making rare earth doped optical fibre which obviates the drawbacks as detailed above.
  • Another object of the present invention is to provide a method of fabricating RE doped preforms and optical fibres by using RE coated silica nanoparticles as precursors.
  • Yet another object in an embodiment of the present invention, is to disperse the rare-earth coated silica nanoparticles in sol under sonication containing germanium tetraethoxide and aluminium salt.
  • Still another object, in an embodiment of the present invention, of the present invention is to control the viscosity of the sol and apply a sol-gel thin film inside high purity silica glass tube by the dip coating technique.
  • Yet another object, in an embodiment of the present invention, of the present invention is to optimize the lifting speed for controlling the thickness of the coating to maintain the desired clad-core dimensions in the preform.
  • Yet another object, in an embodiment of the present invention, of the present invention is to optimize the leading percentage of the nanoparticles and other codopants in the sol.
  • Yet another object, in an embodiment of the present invention, is to reduce the number of steps of the process to make the process more simple and economic.
  • Yet another object, in an embodiment of the present invention, of the present invention it to reduce the requirement of precision equipments for fabrication and consequently reduce the capital investment and cost of the product.
  • Still another object, in an embodiment of the present invention, of the present invention is to provide a process where the numerical aperture of the fibre is varied from 0.10 to 0.30 maintaining RE concentration in the core between 50 to 5000 ppm along to produce fibres suitable for application as amplifiers, fibre lasers and sensors for different purposes.
  • the novelty of the present invention lies in eliminating the step of the formation of porous soot layer at high temperate (1000°C or above) by CVD process inside a fused silica glass tube for formation of the core. Instead a thin silica gel coating containing other dopants in desired proportions is applied through a silica sol at ambient temperature.
  • the above method ensures a better control of the characteristics of the coated layer and uniformity along the length of the tube.
  • the inventive step further includes elimination of the step of the incorporation of the rare-earth ions into the porous soot layer following the solution-doping technique.
  • the rare-earth oxide coated silica nanoparticles are dispersed at ambient temperature in the silica sol mentioned above under sonication thereby further eliminating the formation of microcrystallites and clusters of rare-earth ions.
  • the elimination of the possibility of evaporation of RE salts at high temperatures due to the direct addition of RE oxides is another inventive step of the process which prevents change in composition including variation of RE concentration in the core and also reduces the possibility of formation of RE dip at the core centre.
  • the present invention provides a process for making rare earth doped optical fibre using stable dispersions (sol) of rare earth (RE) oxide coated silica nanoparticles and applying a thin coating of the said silica sol containing suitable dopants selected from Ge, Al, P etc., on the inner surface of a silica glass tube.
  • the RE oxide is selected from Eu 2 O 3 , Nd 2 O 3 , Tb 2 O 3 and Er 2 O 3 for preparation of the silica nanoparticles.
  • P 2 O 5, and F doped synthetic cladding is deposited within a silica glass substrate tube prior to development of the coating by known method like Modified Chemical Vapour Deposition (MCVD) process to obtain matched or depressed clad type structure in the preform.
  • MCVD Modified Chemical Vapour Deposition
  • particle size of the RE coated SiO 2 powders ranges from 50 to 200 nm.
  • the composition in oxide mol% of SiO 2 : RE 2 O 3 in RE 2 O 3 coated SiO 2 powders varies from 99.5 : 0.5 to 95 : 5.
  • the equivalent oxide mol% of SiO 2 in the dispersion varies from 98.5 to 90.5.
  • a silica sol prepared with Si(OC 2 H 5 ) 4 was used as the diluent of the RE 2 O 3 coated silica powder.
  • the equivalent oxide mol% of GeO 2 in the dispersion varies from 1.0 to 5.0.
  • GeO 2 was added through Ge(OC 2 H 5 ) 4 in the silica sol.
  • the equivalent oxide mol% of Al 2 O 3 in the dispersion ranges from 0.5 to 4.0.
  • Al 2 O 3 is provided to the solvent in the form of aluminium salts such as chlorides, nitrates or any other salt soluble in the solvent.
  • the solution of aluminium salt is prepared using a solvent selected from alcohol and water.
  • the oxide mol% of RE 2 O 3 in the dispersion ranges from 0.01 to 0.60.
  • strong mineral acids used for preparing the sol for dispersion are selected from hydrochloric or nitric acid.
  • the alcohol selected is soluable in the dispersion system.
  • the alcohol is selected from the group comprising of methyl alcohol, ethyl alcohol, propan-1-ol, propan-2-ol, butan-1-ol and butan-2-ol.
  • pH of the dispersion ranges from 1 to 5.
  • viscosity of the dispersion varies from 1 to 10 mPa s.
  • sonication time of the dispersion ranges from 30 to 200 minutes.
  • settling time of the dispersion varies from 1 to 10 hours.
  • lifting speed of the tube from the dispersion ranges from 4 to 15 cm/min.
  • baking temperature of the coated tube varies from 70° to 150°C.
  • baking time of the coated tube ranges from 0.5 to 5 h.
  • the core composition is selected from the group comprising of RE 2 O 3 +SiO 2 +GeO 2 , RE 2 O 3 +SiO 2 +GeO 2 +Al 2 O 3 , RE 2 O 3 +SiO 2 +GeO 2 +Al 2 O 3 +P 2 O 5 and RE 2 O 3 +SiO 2 +GeO 2 + P 2 O 5 .
  • the temperature of the RE oxide containing core layer is increased in steps of 50 to 200°C during sintering depending on the composition and Al/RE concentration of the core layer.
  • the mixture of O 2 and He is in the range of 3:1 to 9:1 during sintering.
  • source of chlorine is CCl 4 where helium is used as carrier gas.
  • the proportion of Cl 2 : O 2 during drying varies from 1.5 : 1 to 3.5 : 1.
  • the dehydration period lies between 1 to 2 hours.
  • the core layer is sintered in the presence of germania to facilitate germania incorporation and to obtain appropriate numerical aperture value.
  • germania is supplied to the core layer during sintering by including GeCl 4 with the input oxygen.
  • the sintering is carried out at a temperature of 1200°C to 1400°C.
  • POCl 3 is added to the input gas mixture during sintering.
  • the core layer is doped with P 2 O 5 to facilitate RE incorporation.
  • P 2 O 5 and GeO 2 concentrations vary from 0.5 to 5.0 mol% and 3.0 to 25.0 mol% respectively in the RE doped core layer of the preform.
  • the numerical aperture of the fibre is varied from 0.10 to 0.30.
  • RE concentration in the core is maintained in the range of 50 to 4000 ppm to produce fibres suitable for application as amplifiers, fibre lasers and sensors or different purposes.
  • codopants like Al and other rare earths are added to the core doped with a selected RE to fabricate fibres containing various dopants in the core in the concentration range of 50 to 5000 ppm and numerical aperture varying between 0.10 and 0.30.
  • the deposition of a porous soot layer at high temperature (1000°C or above) by CVD process inside a fused silica glass tube or on a seed rod (VAD or OVD apparatus) is eliminated for formation of the core.
  • the rare-earth oxide coated silica nanoparticles are dispersed at ambient temperature in the silica sol mentioned above under sonication thereby eliminating the possibility of formation of the microcrystallites and clusters of rare-earth ions as in the conventional techniques.
  • the process ensures better control of RE concentration in the doped region and homogeneous distribution of RE ions along the radial direction as well as throughout the length of the preform.
  • the RE incorporation efficiency is much higher compared to the conventional techniques beacuse of direct addition of the RE oxides into the dispersion instead of the corresponding salt by the conventional techniques thereby minimising the possibility of evaporation and change in concentration.
  • the processing of the tube at ambient temperature before sintering and collapsing instead of high temperature involved in the CVD process makes the process less sensitive to the process parameters unlike the conventional processes.
  • Amorphous silica microspheres in the size range of 50-250 nm were synthesized by the alkaline hydrolysis of tetraethoxysilane (Stober method).
  • Stober method tetraethoxysilane
  • nanophased rare earth oxides were sonochemically deposited on the outer surface of spherical silica particles.
  • rare earth nitrate used as the source of rare earth was prepared by dissolving rare earth oxide in a minimum amount of nitric acid followed by evaporating it to dryness. The dry nitrate was dissolved in calculated quantity of water to prepare the rare earth nitrate solution.
  • silica microspheres The required amount of silica microspheres was taken in a beaker and calculated quantity of water and rare earth nitrate solution, as prepared earlier, were then added to it.
  • the open beaker with the material was kept in an ice-bath and subjected to sonication for 1h employing a direct immersion titanium horn (Vibracell, 20 kHz, 100 W/cm 2 ).
  • Required amount of 25% aqueous ammonia was thereafter added in drops into the beaker during sonication.
  • the resulting product after sonication was washed thoroughly with water, centrifuged and finally dried under vacuum to obtain RE coated amorphous silica nanoparticles.
  • the above method is also suitable for the preparation of doped and co-doped silica particles containing Al 2 O 3 , GeO 2 , Yb 2 O 3 and other rare earth oxides.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Chemical Kinetics & Catalysis (AREA)
  • Materials Engineering (AREA)
  • General Chemical & Material Sciences (AREA)
  • Geochemistry & Mineralogy (AREA)
  • Life Sciences & Earth Sciences (AREA)
  • Organic Chemistry (AREA)
  • General Life Sciences & Earth Sciences (AREA)
  • Manufacturing & Machinery (AREA)
  • Dispersion Chemistry (AREA)
  • Glass Compositions (AREA)
  • Manufacture, Treatment Of Glass Fibers (AREA)
  • Lasers (AREA)
EP01978809A 2001-10-18 2001-10-18 A process of making rare earth doped optical fibre Expired - Lifetime EP1441991B1 (en)

Priority Applications (1)

Application Number Priority Date Filing Date Title
AT01978809T ATE317375T1 (de) 2001-10-18 2001-10-18 Verfahren zur herstellung einer mit seltenen erden dotierten optischen faser

Applications Claiming Priority (1)

Application Number Priority Date Filing Date Title
PCT/IN2001/000184 WO2003033423A1 (en) 2001-10-18 2001-10-18 A process of making rare earth doped optical fibre

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EP1441991A1 EP1441991A1 (en) 2004-08-04
EP1441991B1 true EP1441991B1 (en) 2006-02-08

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EP (1) EP1441991B1 (zh)
JP (1) JP4141956B2 (zh)
KR (1) KR100816010B1 (zh)
CN (1) CN100503494C (zh)
DE (1) DE60117161D1 (zh)
WO (1) WO2003033423A1 (zh)

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CN107188404B (zh) * 2017-07-17 2020-04-17 江苏亨通光导新材料有限公司 一种使用有机硅制备高质量光纤预制棒的方法
CN110981183B (zh) * 2019-12-16 2021-04-27 长飞光纤光缆股份有限公司 一种宽带多模光纤预制棒的制造方法
CN110937796B (zh) * 2019-12-16 2021-04-27 长飞光纤光缆股份有限公司 宽带多模光纤预制棒的制造方法
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CN117358926B (zh) * 2023-12-05 2024-02-13 天津大学 一种锗光阑阵列的制备方法及光场成像系统

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JP4141956B2 (ja) 2008-08-27
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